EP1394276B1 - Feuille d'acier laminee a chaud a haute resistance, presentant une resistance a l'usure sur moule et des caracteristiques de fatigue excellentes - Google Patents

Feuille d'acier laminee a chaud a haute resistance, presentant une resistance a l'usure sur moule et des caracteristiques de fatigue excellentes Download PDF

Info

Publication number
EP1394276B1
EP1394276B1 EP02778909A EP02778909A EP1394276B1 EP 1394276 B1 EP1394276 B1 EP 1394276B1 EP 02778909 A EP02778909 A EP 02778909A EP 02778909 A EP02778909 A EP 02778909A EP 1394276 B1 EP1394276 B1 EP 1394276B1
Authority
EP
European Patent Office
Prior art keywords
mass
steel sheet
less
temperature
steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Fee Related
Application number
EP02778909A
Other languages
German (de)
English (en)
Other versions
EP1394276A1 (fr
EP1394276A4 (fr
Inventor
T. c/o Intellectual Property Dpt. MEGA
K. c/o Intellectual Property Dpt. SAKATA
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP1394276A1 publication Critical patent/EP1394276A1/fr
Publication of EP1394276A4 publication Critical patent/EP1394276A4/fr
Application granted granted Critical
Publication of EP1394276B1 publication Critical patent/EP1394276B1/fr
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling

Definitions

  • This invention relates to a high-strength hot rolled steel sheet having a tensile strength of not less than 590 MPa and excellent anti-die-galling property and anti-fatigue property which is suitable for use mainly in structural parts of automobiles, underbody parts such as a wheel, a rim and a chassis, high-strength parts such as a bumper and a door guard bar, and so on as hot-rolled.
  • the hot rolled steel sheets which are used in the structural part of the automobile, underbody parts such as a wheel, a rim and a chassis, high-strength parts such as a bumper and a door guard bar, and so on.
  • high-strength steel sheets having a tensile strength of not less than 590 MPa.
  • the hot rolled steel sheets used in such applications are required to have a good anti-fatigue property.
  • the underbody parts supporting the weight of the vehicle body are required to have an excellent anti-fatigue property in the bending mode because a large bending deformation is applied to the steel sheet.
  • JP-A-55-28375 proposes a steel sheet having an improved shape fixability in which it is made possible to lower the yield point as compared with the degree of the tensile strength by dispersing hard martensite into soft ferrite to form a dual phase microstructure.
  • a technique for improving the press formability by properly adjusting the surface roughness of the steel sheet as mentioned above is disclosed in, for example, JP-A-6-99202 .
  • This technique ensures good frictional characteristics and improves the press formability by adjusting the surface roughness, which is provided by the control of a skin pass rolling, in accordance with the strength of the steel sheet with respect to thin steel sheets produced by the continuous annealing.
  • JP-A-6-99202 targets steel sheets having inherently a small surface roughness such as cold rolled steel sheets and surface treated steel sheets, so that there is a problem that it is difficult to apply the above technique to steel sheets having inherently a large surface roughness resulted from the push-in of scale or the like during the rolling such as hot rolled steel sheets.
  • JP-A-9-118918 a technique providing the hot rolled steel sheet suitable for use in applications for working and forming such as a stamping or the like by adjusting the surface roughness of the steel sheet is disclosed in JP-A-9-118918 .
  • This technique intends to improve the frictional characteristics and the ductility by rendering the surface roughness of at least one surface of the steel sheet into Ra of not more than 0.8 ⁇ m, Rmax of not more than 4.0 ⁇ m and Rv/Rmax of not more than 0.7.
  • the term "Rv" used herein means a distance from a deepest valley to a center line in a measured length of a profile curve.
  • JP-A-7-150 291 discloses that a cast ingot having a composition containing, by weight, 0.05 to 0.20% C, 0.20 to 2.0% Si, 0.60 to 2.5% Mn, 0.005 or below S, 0.10% or below P and 0.10% or below Al or moreover containing specified small amounts of one or more kinds of elements among Cu, Ni, Cr, Mo, V, Ti, Nb, B, Ca or the like is subjected to rough rolling and is thereafter subjected to hot rolling to form a hot rolled steel sheet, e.g. having 3.5 mm thickness.
  • the structure of this hot rolled sheet is formed of three phases of polygonal ferrite, bainite and martensite, and the high strength hot rolled steel sheet for working having a structure in which the bainitic volume fraction (VfB) is regulated to 1 to 15%, the martensitic volume fraction (VfM) is regulated to 2 to 30% and the ratio of VfM/VfB is regulated to 2 to 20 and excellent in a balance of strength-elongation, stretch flanging properties and fatigue properties can be obtained.
  • VfB bainitic volume fraction
  • VfM martensitic volume fraction
  • JP-A-9-143 612 discloses that a steel having a chemical composition containing by weight, 0.05 to 0.25% C, 0.01% to 1.0% Si, 0.50 to 2.0% Mn, 0.05% or below P, 0.03% or below S, 0.08% or below sol.Al and 0.01% or below N, and the balance Fe with inevitable impurities is subjected to hot rolling and is coiled, and after that, the steel plate is subjected to cold working, is thereafter reheated to a ferrite-austenite coexistent temperature region and is subjected to hot forming to form its structure after cooling into a mixed one essentially consisting of ferrite and martensite.
  • JP-A-10-195 588 discloses that as for a steel stock having a componental composition containing by weight, 0.02 to 0.2% C, 0.1 to 1.5% Si, 0.5 to 3.0% Mn and 0.010% or below S, furthermore containing one or more kinds selected from 0.03 to 0.15% Mn, 0.1 to 2.0% Cr and 0.1 to 1.0% Mo, and the balance Fe with inevitable impurities, hot rolling is finished at the Ar 3 transformation point or above, within 0.1 to 5.0 sec after that, cooling is started, it is cooled to 620 to 800°C at a cooling rate 50°C/sec or more, is subjected to air cooling for 0.5 to 15 sec, is next cooled to 300 to 600°C at a cooling rate of 30°C/sec or more and is coiled to form its structure into the one in which ferritic phases having average grain size of 10 ⁇ m or below, occupy by 80 to 97 vol.%; and the balance secondary phases essentially consisting of martensite in which the average diameter is regulated to 0.2
  • an object of the invention to solve the aforementioned problems of the conventional techniques and to provide a high-strength hot rolled steel sheet having not only an excellent press formability but also an excellent anti-die-galling property and a good anti-fatigue property and having a tensile strength of not less than 590 MPa as well as a method of advantageously producing the same.
  • the invention is based on the above knowledge.
  • C is an element useful for improving the tensile strength, and C content is required to be at least 0.02 mass% in order to obtain a desired tensile strength.
  • the C content exceeds 0.2 mass%, CO gas is generated at an interface between the scale and the base iron to cause the occurrence of scale flaw at the rolling stage and the arithmetic mean roughness Ra becomes larger but also the weldability is drastically deteriorated. Therefore, the C content is limited to a range of not less than 0.02 mass% but not more than 0.2 mass%. Preferably, it is not less than 0.02 mass% but not more than 0.12 mass%.
  • Si not less than 0.2 mass% but not more than 1.2 mass%
  • Si is an element being large in the solid solution hardening and contributing to increase the strength of the steel without damaging the yield ratio and the balance between the strength and the elongation. And also, it is an element essential for the formation of the mixed microstructure by activating a transformation from ⁇ to ⁇ to promote C enrichment into ⁇ phase and also effectively contributes to the cleaning of the steel as a deoxidizing element in the steel making. Further, it is an essential element in steel for controlling the formation of a carbide such as Fe 3 C or the like to facilitate the formation of the dual phase microstructure consisting of ferrite and martensite and lower the yield ratio. Moreover, it has an action that it is solid-soluted into ferrite to increase the tensile strength and strengthen grains of soft ferrite to thereby improve the anti-fatigue property.
  • a carbide such as Fe 3 C or the like
  • the Si content is limited to a range of not less than 0.2 mass% but not more than 1.2 mass%. Preferably, it is not less than 0.6 mass% but not more than 1.2 mass%.
  • Mn not less than 1.0 mass% but not more than 3.0 mass%
  • Mn is a useful element not only effectively contributing to the improvement of the strength of the steel but also improving the hardenability, and particularly it is an effective element for rendering the second phase into the microstructure comprising the martensite phase. Moreover, it has an effect for precipitating the solid-soluted S, which causes the brittleness fracture in the hot working, as MnS to defuse it.
  • Mn content is less than 1.0 mass%. While, when the Mn content exceeds 3.0 mass%, it has various bad influences that the scale is stabilized on the steel surface not only to generate the surface flaw and make the surface roughness too large but also to deteriorate the weldability and the like. Therefore, the Mn content is limited to a range of not less than 1.0 mass% but not more than 3.0 mass%. Preferably, it is not less than 1.0 mass% but not more than 2.5 mass%.
  • Mo is a useful element for not only contributing to the improvement of the strength of the steel but also improving the hardenability to facilitate the formation of the microstructure comprised of ferrite and martensite and lowering the yield ratio to improve the anti-die-galling property. And also, Mo is the element having an effect that the crystal grains in steel are fined to improve the balance between the strength and the elongation but also reduce the surface roughness. In the hot rolled steel sheet, the crystal grain size in the surface layer portion of the steel sheet generally tends to become larger as compared with the crystal grain size in the center portion of the steel sheet.
  • Ar 3 transformation point is raised by adding Mo and further the rolling is carried out just above the Ar 3 transformation point, whereby there can be prevented that the crystal grain size of the surface layer portion of the steel sheet becomes larger as compared with that of the center portion of the steel sheet. That is, it is tendentious that the surface layer portion of the steel sheet can be rolled in a dual phase region of ⁇ and ⁇ and the center portion of the steel sheet can be rolled in a ⁇ region, so that the crystal grain in the surface layer portion of the steel sheet can be made finer as compared with that in the center portion of the steel sheet. Therefore, the anti-die galling property can be improved and also the anti-fatigue property in the bending mode can be improved.
  • Mo content is necessary to be not less than 0.1 mass%.
  • Mo content exceeds 1.0 mass%, bainite is formed, which further brings about the bad influence such as the deterioration of the weldability or the like. Therefore, the Mo content is limited to a range of not less than 0.1 mass% but not more than 1.0 mass%.
  • Al is a useful element as a deoxidizing agent.
  • Al content is less than 0.01 mass%, the addition effect becomes poor.
  • the Al content exceeds 0.1 mass%, the effect is saturated and also the increase of the cost and the embrittlement of the steel sheet are caused. Therefore, the Al content is limited to a range of not less than 0.01 mass% but not more than 0.1 mass%.
  • the content is an element deteriorating the weldability and causing the embrittlement of the grain boundary, it is preferable to reduce the content as far as possible.
  • the P content exceeds 0.03 mass%, the deterioration of the weldability or the like appears remarkably, so that the upper limit of the P content is 0.03 mass%.
  • the lower limit of the P content capable of reducing without causing the remarkable increase of the steel-making cost in the existing refinement technique is about 0.005 mass%.
  • the upper limit of the S content is 0.01 mass%. More preferably, the Si content is not more than 0.007 mass%. Moreover, the lower limit of the S content capable of reducing without causing the remarkable increase of the steel-making cost in the existing refinement technique is about 0.001 mass%.
  • Cr is a useful element for improving the hardenability but also contributing to increase the strength of the steel as a solid-soluted element. And also, Cr also contributes to the formation of the dual phase microstructure of the ferrite and the martensite and is a useful element for controlling the pearlite transformation to stabilize the austenite phase as a second phase during the hot rolling and ensure the martensite after the hot rolling.
  • Cr content is preferable to be not less than 0.1 mass%.
  • the Cr content exceeds 0.3 mass%, a stable Cr oxide phase is formed on the steel surface to obstruct the descaling property, and the surface roughness of the steel sheet becomes larger and not only phosphatability is remarkably deteriorated but also the weldability is adversely affected and further the cost increases. Therefore, the Cr content is limited to not more than 0.3 mass%.
  • Ca has an action of fining the sulfide form and is a useful element contributing to improve the elongation and the anti-fatigue property.
  • the Ca content is required to be not less than 0.001 mass%.
  • the Ca content exceeds 0.005 mass%, the effect is saturated and the cost is unnecessarily increased and the cleanliness of steel is inversely deteriorated. Therefore, the Ca content is limited to a range of not less than 0.001 mass% but not more than 0.005 mass%.
  • the REM (rare earth element) has an action of fining the sulfide form and is a useful element contributing to improve the elongation and the anti-fatigue property likewise Ca.
  • the REM content is required to be not less than 0.001 mass%.
  • the REM content exceeds 0.005 mass%, the effect is saturated and the cost is unnecessarily increased and the cleanliness of steel is inversely deteriorated. Therefore, the REM content is limited to a range of not less than 0.001 mass% but not more than 0.005 mass%.
  • the remainder other than the above elements is Fe and inevitable impurities.
  • the microstructure of the steel forms the ferrite as a main phase by rendering the ferrite into not less than 55 vol% and produces the martensite within a range of not less than 10 vol% but not more than 40 vol%.
  • the yield ratio is lowered to facilitate the deformation at the surface layer portion of the steel sheet and also the pressure at a contact portion between the mold and the steel sheet in the press forming is lowered, whereby the anti-die galling property can be improved.
  • the above effects can not be obtained.
  • the martensite is also required to be not less than 10 vol%. However, when it exceeds 40 vol%, the effect is saturated and the strength is remarkably increased to lower the ductility.
  • bainite and the like can be included up to 5 vol% as the other microstructure.
  • the total amount of the ferrite and the martensite is not less than 95 vol%. Moreover, when the total amount of the ferrite and the martensite is less than 95 vol%, the influence of the mixed other phase becomes larger and hence it is difficult to sufficiently obtain the above effects by the ferrite and the martensite.
  • the ratio ds/dc of the average crystal grain size ds of the ferrite in a region ranging from the surface of the steel sheet to a position corresponding to a quarter-thickness in the steel sheet, that is, in the surface layer portion of the steel sheet to the average crystal grain size dc of the ferrite in a region ranging from the position corresponding to the quarter-thickness in the steel sheet to a center of the thickness, that is, in the center portion of the steel sheet is more than 0.3 but not more than 1.0.
  • a position corresponding to a quarter-thickness in the steel sheet means a position located inside the steel sheet by a quarter of the overall thickness from the surface of the steel sheet.
  • the strength of the steel is inversely proportional to the crystal grain size by means of the Hall-Petch relationship.
  • the crystal grain size in the surface layer portion of the steel sheet so as not to make larger than the crystal grain size in the center portion of the steel sheet can be made the strength in the surface layer portion of the steel sheet equal to or larger than the strength in the center portion of the steel sheet.
  • the ratio ds/dc of the above average crystal grain sizes is not more than 0.3, the crystal grains in the center portion of the steel sheet are remarkably coarsened and hence the sufficient strength of the steel sheet is not obtained, and also the difference in the strength between the surface layer portion of the steel sheet and the center portion of the steel sheet becomes larger, and the die-galling due to the mold in the press forming is increased to lower the anti-die-galling property.
  • the surface roughness is necessary to be not more than 1.5 ⁇ m as an arithmetic mean roughness Ra.
  • surface roughness used herein means a surface roughness in a direction of 90° with respect to the hot rolling direction.
  • Ra exceeds 1.5 ⁇ m, both the anti-die-galling property and the anti-fatigue property deteriorate and even if the microstructure of the steel sheet is adjusted as mentioned above, the effects for improving the anti-die-galling property and the anti-fatigue property can not be obtained.
  • the preferable range of the surface roughness is not less than 0.8 ⁇ m but not more than 1.2 ⁇ m as the arithmetic mean roughness Ra.
  • the hot rolling is conducted under a condition that the final deformation temperature is not lower than (Ar 3 transformation point-100°C) but lower than Ar 3 transformation point as a surface temperature.
  • the surface layer portion of the steel sheet is mostly rolled in the dual phase region of ⁇ and ⁇ , while the center portion of the steel sheet is mostly rolled in the ⁇ region, and hence the crystal grain size in the surface layer portion of the steel sheet can be adjusted so as not to make larger than the crystal grain size in the center portion of the steel sheet.
  • a more preferable range of the final deformation temperature is a range of not lower than (Ar 3 transformation point-50°C) but lower than Ar 3 transformation point as a surface temperature.
  • the thickness of the hot rolled steel sheet is not especially limited, but is preferable to be not less than 2.0 mm but not more than 5.0 mm.
  • the steel sheet is cooled to a temperature range of not higher than 750°C but not lower than 700°C, kept at this temperature range for not less than 2 seconds but not more than 30 seconds, cooled and then coiled at not higher than 650°C but not lower than 500°C.
  • cooling to the temperature range of not higher than 750°C but not lower than 700°C can be promoted the ferrite transformation and also the enrichment of C into the ⁇ phase is promoted to facilitate the formation of the martensite phase.
  • the ferrite transformation is delayed by deviating from a precipitation nose of the ferrite phase in the course of a moderate cooling, i.e. in the retention at the temperature region of not higher than 750°C but not lower than 700°C and hence the dual phase separation of ⁇ and ⁇ is not promoted.
  • a preferable range of the cooling temperature is not higher than 730°C but not lower than 720°C.
  • the cooling rate does not need to be especially limited, but it is preferable to be not less than 15°C/s but not more than 40°C/s as an average cooling rate.
  • the retention at this temperature range for not less than 2 seconds but not more than 30 seconds contributes to the promotion of the dual phase separation of ⁇ and ⁇ , which is important for obtaining the finally targeted dual phase microstructure of the ferrite and the martensite.
  • the retention time is less than 2 seconds, the dual phase separation from ⁇ to ⁇ does not proceed, and the enrichment of C into ⁇ is not sufficient and the martensite transformation of the second phase hardly occurs in the subsequent coiling step, and hence the target microstructure is not obtained.
  • the retention treatment may be either a retaining treatment keeping at a constant temperature or a so-called moderate cooling treatment slowly cooling within the temperature range such as air cooling or the like. More preferably, the retention time is not less than 5 seconds but not more than 10 seconds.
  • the steel sheet is cooled and coiled at not higher than 650°C but not lower than 500°C to form a hot rolled steel sheet.
  • the cooling rate does not need to be limited, but it is preferable to be not less than 15°C but not more than 40°C/s.
  • the reason why the coiling temperature is limited to not higher than 650°C but not lower than 500°C is based on the following fact. When it exceeds 650°C, the pearlite is produced to considerably suppress the formation of the martensite and hence the target microstructure can not be obtained. In addition, the scale growth after the coiling occurs, and the pickling property is poor and the roughness in the surface of the base iron becomes larger due to the excessive oxidization.
  • the steel sheet when it is lower than 500°C, the steel sheet easily renders into an undulating shape due to the lowering of the coiling temperature and the control therefor becomes difficult. Also, the surface flaw easily occurs in the coiling step and hence the arithmetic mean roughness Ra becomes too large. Furthermore, the strength is remarkably increased to bring about the remarkable deterioration of the press formability and there may be caused a case that a large amount of the bainite phase is included in the microstructure, so that the formation of the martensite is restrained to bring about the increase of the yield ratio.
  • a preferable range of the coiling temperature is not higher than 600°C but not lower than 550°C.
  • the cooling rate after the coiling is not especially limited, but the cooling in air is sufficient because in the invention, the sufficient enrichment of C into the austenite phase is achieved by coiling at the above temperature range.
  • the dual phase separation of ⁇ and ⁇ is promoted to promote the formation of the dual phase microstructure of ⁇ and ⁇ .
  • the slab heating temperature before the hot rolling is not especially limited and is sufficient to be not lower than 1100°C but not higher than 1250°C as a usual range.
  • the crystal grain size in the surface layer portion of the steel sheet can be adjusted so as not to make larger than the crystal grain size in the center portion of the steel sheet.
  • a steel slab having a preferable composition as mentioned above is used as a starting material and subjected to a hot rolling under conditions that the slab reheating temperature is not higher than 1100 °C and the final deformation temperature is not lower than (Ar 3 transformation point-100°C) but not higher than (Ar 3 transformation point+50°C) as a surface temperature.
  • the slab reheating temperature is not higher than 1100 °C
  • the final deformation temperature is not lower than (Ar 3 transformation point-100°C) but not higher than (Ar 3 transformation point+50°C) as a surface temperature.
  • the scale is formed on the surface of the slab by solute elements such as Fe, Mn, Si and the like diffusing from the inside of the slab through ⁇ grain boundary and an oxygen introduced from the atmosphere (air).
  • solute elements such as Fe, Mn, Si and the like diffusing from the inside of the slab through ⁇ grain boundary and an oxygen introduced from the atmosphere (air).
  • the higher the temperature is the larger the diffusion rate of the solute elements of Fe, Mn, Si and the oxygen into the ⁇ grain boundary is, and the scale largely growing at ⁇ grain boundary is particularly formed to make the unevenness on the surface larger.
  • it exceeds 1100°C the formation of the unevenness becomes remarkable and it is difficult to render the arithmetic mean roughness Ra into not more than 1.5 ⁇ m.
  • the slab reheating temperature is made to not higher than 1100°C, the surface roughness becomes smaller while the crystal grain size in the surface becomes smaller. As a result, there are obtained the effects of improving not only the anti-die-galling property but also the anti-fatigue property in the bending mode. Moreover, the slab heating temperature is more preferable to be not higher than 1050°C.
  • the crystal grain size in the surface layer portion of the steel sheet can be done so as not to make larger than the crystal grain size in the center portion of the steel sheet.
  • the ferrite transformation is promoted to form the coarse grains on the surface layer.
  • the steel sheet After the hot rolling, the steel sheet is cooled at a rate of not less than 40°C/s to a temperature range of not higher than 750°C but not lower than 700°C.
  • cooling rate used herein means an average cooling rate until the cooling is finished at the temperature range of not higher than 750°C but not lower than 700°C after the completion of the hot rolling.
  • the cooling rate after the hot rolling into not less than 40°C/s, even when the final deformation temperature is not higher than Ar 3 +50°C even in not only the range of not lower than (Ar 3 -100°C) but lower than Ar 3 but also not lower than Ar 3 , the growth of the recrystallized ⁇ grains after the rolling is suppressed and a greater quantity of strain is stored in the steel, particularly, in the vicinity of the surface thereof by an effect of the supercooling to largely introduce nuclei in the transformation from ⁇ to ⁇ and hence refine the ferrite grains.
  • the crystal grain size in the surface layer portion of the steel sheet can be made smaller than the crystal grain size in the center portion of the steel sheet, whereby the anti-fatigue property in the bending mode can be improved while improving the anti-die-galling property.
  • the cooling rate after the hot rolling is preferable to be not less than 50°C/s.
  • the steel sheet after the hot rolling is subjected to a pickling to form a pickled hot rolled steel sheet.
  • the pickling method is not especially limited and may be conducted in the usual manner.
  • a skinpass rolling (a rolling reduction: not more than about 1%) may be conducted for the correcting of the form, if necessary.
  • Each of steels having various compositions shown in Table 1 is rendered into a hot rolled steel sheet under conditions shown in Table 2. Moreover, the thickness of the hot rolled steel sheet is 2.7 mm and all of the hot rolled steel sheets are subjected to the pickling after the hot rolling but are not subjected to the skinpass rolling.
  • the microstructure of the steel, the average crystal grain sizes of the ferrite in both the center portion of the steel sheet and the surface layer portion of the steel sheet and ratio ds/dc of them, the surface roughness Ra, and the tensile characteristics (yield strength (YS), tensile strength (TS), elongation (El), yield ratio (YR YS/TS), anti-die-galling property, anti-fatigue property (endurance ratio (ratio of fatigue strength ⁇ w to tensile strength TS)) and the phosphatability (weight of chemical-treated coating) are investigated to obtain results shown in Table 3.
  • the microstructure of steel is evaluated by observing a section of a test piece sampled from the hot rolled steel sheet in a direction parallel to the rolling direction over the overall thickness thereof by means of an electron microscope and conducting an image analysis of the resulting photograph to measure each texture fraction in the microstructure as a volume percentage. And also, the average crystal grain size of the ferrite is measured according to a cutting method disclosed in a method of testing the crystal grain size number of ferrite in steel shown in JIS G0552 after the shooting with the electron microscope.
  • ds is an average crystal grain size of the ferrite measured in the surface layer portion of the steel sheet, i.e. in both a region from a front surface side of the steel sheet to a position corresponding to the quarter-thickness in the steel sheet and a region from a back surface side of the steel sheet to a position corresponding to the quarter-thickness in the steel sheet.
  • dc is an average crystal grain size of the ferrite measured in a region ranging from the quarter-thickness positions at the front and back surface sides of the steel sheet to a center position in the thickness, i.e. in a center portion of the steel sheet existing over a half of the overall thickness.
  • the surface roughness of the hot rolled steel sheet in a direction of 90° with respect to the rolling direction is measured as an arithmetic mean roughness Ra according to JIS B0601.
  • the tensile characteristics are measured by a tensile test using a JIS No. 5 tensile test piece sampled from the hot rolled steel sheet after the pickling in a direction of 90° with respect to the rolling direction.
  • the anti-fatigue property is evaluated by measuring an endurance ratio ⁇ W/TS of fatigue strength ⁇ W to tensile strength TS according to a plane bending test of perfectly alternating load (JIS Z2275) complying with a repeated bending test under completely reversed plane bending (JIS Z 2275) when stress not broken after repeated load of 107 times is a fatigue strength ⁇ W.
  • JIS Z2275 perfectly alternating load
  • JIS Z 2275 completely reversed plane bending
  • the phosphatability is evaluated by washing and degreasing the steel sheet (mass W 0 ) as a test material, immersing in a solution containing a chemical-treating agent (zinc phosphate solution) for a given period of time, further washing, and then measuring a mass (W) to calculate a mass increment (W-W 0 ) per unit area through the adhesion of zinc phosphate crystal, i.e. a weight of a chemical-treated coating.
  • the target value is not less than 2.0 g/m 2 .
  • the tensile strength TS is not less than 590 MPa and the yield ratio YR is less than 70% and also the anti-die-galling property and anti-fatigue property are excellent and the phosphatability is good as compared with those of the other steels.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (4)

  1. Feuille d'acier laminée à chaud à haute résistance ayant une propriété anti-grippage de la matrice et une propriété anti-fatigue excellentes, caractérisée en ce que la feuille d'acier a une composition comprenant : C : pas moins de 0,02 % en masse mais pas plus de 0,2 % en masse, Si : pas moins de 0,2 % en masse mais pas plus de 1,2 % en masse, Mn : pas moins de 1,0 % en masse mais pas plus de 3,0 % en masse, Mo : pas moins de 0,1 % en masse mais pas plus de 1,0 % en masse, Al : pas moins de 0,01 % en masse mais pas plus de 0,1 % en masse, P : pas plus de 0,03 % en masse et S : pas plus de 0,01 % en masse, contenant facultativement au moins un élément choisi parmi Cr : pas plus de 0,3 % en masse, Ca : pas moins de 0,001 % en masse mais pas plus de 0,005 % en masse et éventuellement REM : pas moins de 0,001 % en masse mais pas plus de 0,005 % en masse et le reste étant Fe et des impuretés inévitables, et a une microstructure d'acier ne contenant pas moins de 55 % en volume de ferrite et pas moins de 10 % en volume mais pas plus de 40 % en volume de martensite, étant entendu qu'un total des deux n'est pas inférieur à 95 % en volume et qu'un rapport ds/dc d'une taille moyenne de grains cristallins ds de la ferrite dans une région allant depuis une surface de la feuille d'acier jusqu'à une position correspondant à un quart d'épaisseur dans la feuille d'acier sur une taille moyenne de grains cristallins de de la ferrite dans une région allant depuis la position correspondant au quart d'épaisseur dans la feuille d'acier jusqu'à un centre d'une épaisseur dans la feuille d'acier est 0,3 < ds/dc ≤ 1,0, et une rugosité de surface n'est pas supérieure à 1,5 µm en tant que rugosité arithmétique moyenne Ra.
  2. Feuille d'acier laminée à chaud à haute résistance ayant une propriété anti-grippage de la matrice et une propriété anti-fatigue excellentes selon la revendication 1, caractérisée en ce que l'acier contient en outre au moins un élément choisi parmi Cr : pas plus de 0,3 % en masse, Ca : pas moins de 0,001 % en masse mais pas plus de 0,005 % en masse et REM : pas moins de 0,001 % en masse mais pas plus de 0,005 % en masse et le reste étant Fe et des impuretés inévitables.
  3. Procédé de fabrication d'une feuille d'acier laminée à chaud à haute résistance ayant une propriété anti-grippage de la matrice et une propriété anti-fatigue excellentes, qui comprend l'utilisation, en tant que matériau de départ, d'une tôle d'acier ayant une composition telle que définie dans la revendication 1 ou 2, la soumission à un laminage à chaud dans une condition où une température de déformation finale est non inférieure à (Ar3-100 °C) mais inférieure à Ar3 en tant que température de surface, le refroidissement à pas plus de 750 °C mais pas moins de 700 °C, le maintien à cette gamme de températures pendant pas moins de 2 secondes mais pas plus de 30 secondes, le refroidissement, puis l'enroulement à pas plus de 650 °C mais pas moins de 500 °C.
  4. Procédé selon la revendication 3, comprenant les étapes consistant à chauffer la tôle d'acier dans une condition où une température de chauffage de la tôle est non supérieure à 1100 °C, à soumettre à un laminage à chaud dans une condition où une température de déformation finale est non inférieure à (Ar3-100 °C) mais non supérieure à (Ar3+50 °C) en tant que température de surface, à refroidir à une vitesse de refroidissement non inférieure à 40 °C/s jusqu'à pas plus de 750 °C mais pas moins de 700 °C, à maintenir à cette gamme de températures pendant pas moins de 2 secondes mais pas plus de 30 secondes, à refroidir, puis à enrouler à pas plus de 650 °C mais pas moins de 500 °C.
EP02778909A 2001-06-07 2002-05-23 Feuille d'acier laminee a chaud a haute resistance, presentant une resistance a l'usure sur moule et des caracteristiques de fatigue excellentes Expired - Fee Related EP1394276B1 (fr)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP2001171955 2001-06-07
JP2001171955 2001-06-07
JP2002133843A JP4062961B2 (ja) 2001-06-07 2002-05-09 耐型かじり性および耐疲労特性に優れた高張力熱延鋼板およびその製造方法
JP2002133843 2002-05-09
PCT/JP2002/005024 WO2002101099A1 (fr) 2001-06-07 2002-05-23 Feuille d'acier laminee a chaud a haute resistance, presentant une resistance a l'usure sur moule et des caracteristiques de fatigue excellentes

Publications (3)

Publication Number Publication Date
EP1394276A1 EP1394276A1 (fr) 2004-03-03
EP1394276A4 EP1394276A4 (fr) 2006-01-18
EP1394276B1 true EP1394276B1 (fr) 2010-10-27

Family

ID=26616479

Family Applications (1)

Application Number Title Priority Date Filing Date
EP02778909A Expired - Fee Related EP1394276B1 (fr) 2001-06-07 2002-05-23 Feuille d'acier laminee a chaud a haute resistance, presentant une resistance a l'usure sur moule et des caracteristiques de fatigue excellentes

Country Status (7)

Country Link
US (1) US7485194B2 (fr)
EP (1) EP1394276B1 (fr)
JP (1) JP4062961B2 (fr)
KR (1) KR100859303B1 (fr)
CN (1) CN1237189C (fr)
DE (1) DE60238118D1 (fr)
WO (1) WO2002101099A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2618958C2 (ru) * 2012-03-23 2017-05-11 Зальцгиттер Флахшталь Гмбх Улучшаемая сталь без окалины, способ изготовления детали без окалины из этой стали и способ получения горячекатаной полосы из стали

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4502272B2 (ja) * 2005-12-14 2010-07-14 株式会社神戸製鋼所 加工性および疲労特性に優れる熱延鋼板及びその鋳造方法
US20140202677A1 (en) * 2011-09-16 2014-07-24 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Original plate material for heat-exchanging plate and heat-exchanging plate using the same
JP6219199B2 (ja) * 2014-02-27 2017-10-25 株式会社神戸製鋼所 熱交換用プレートとなる元板材、及びその元板材の製造方法
JP5707547B1 (ja) * 2014-03-07 2015-04-30 株式会社宝機材 高張力鋼グレーチングにおける主部材の選択方法
JP6382301B2 (ja) * 2014-03-28 2018-08-29 アベル株式会社 ステンレス鋼板
JP2015169071A (ja) * 2014-10-15 2015-09-28 株式会社宝機材 高張力鋼グレーチングの製造方法
JP6179584B2 (ja) * 2015-12-22 2017-08-16 Ｊｆｅスチール株式会社 曲げ性に優れた高強度鋼板およびその製造方法
JP6394841B1 (ja) * 2017-02-17 2018-09-26 Ｊｆｅスチール株式会社 高強度熱延鋼板およびその製造方法
DE102020134719A1 (de) 2020-12-22 2022-06-23 Aktiebolaget Skf Verfahren zum Herstellen eines Zielobjekthalters für eine Sensorlagereinheit und zugehörige Sensorlagereinheit
DE102020134720A1 (de) * 2020-12-22 2022-06-23 Aktiebolaget Skf Verfahren zum Herstellen eines Zielobjekthalters für eine Sensorlagereinheit

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4466842A (en) * 1982-04-03 1984-08-21 Nippon Steel Corporation Ferritic steel having ultra-fine grains and a method for producing the same
JPS63145717A (ja) * 1986-12-09 1988-06-17 Kobe Steel Ltd 低降伏比高張力鋼板の製造方法
JP3069199B2 (ja) 1992-09-21 2000-07-24 川崎製鉄株式会社 プレス成形性に優れた高張力薄鋼板
JPH06264185A (ja) * 1993-03-09 1994-09-20 Sumitomo Metal Ind Ltd 疲労特性の優れた熱延鋼板およびその製造方法
JP3286050B2 (ja) * 1993-12-01 2002-05-27 株式会社神戸製鋼所 疲労特性に優れた加工用高強度熱延鋼板
JPH0949026A (ja) * 1995-08-07 1997-02-18 Kobe Steel Ltd 強度−伸びバランス及び伸びフランジ性にすぐれる高強度熱延鋼板の製造方法
JPH09118918A (ja) 1995-10-23 1997-05-06 Kawasaki Steel Corp 摺動性および延性に優れる熱延鋼板ならびにその製造方法
JPH09143612A (ja) 1995-11-21 1997-06-03 Kobe Steel Ltd 降伏比の低い高強度熱延鋼板部材
JPH10176239A (ja) * 1996-10-17 1998-06-30 Kobe Steel Ltd 高強度低降伏比パイプ用熱延鋼板及びその製造方法
JP3253880B2 (ja) 1996-12-27 2002-02-04 川崎製鉄株式会社 成形性と耐衝突特性に優れる熱延高張力鋼板およびその製造方法
JP3572894B2 (ja) * 1997-09-29 2004-10-06 Ｊｆｅスチール株式会社 耐衝突特性と成形性に優れる複合組織熱延鋼板およびその製造方法
JPH11279693A (ja) * 1998-03-27 1999-10-12 Nippon Steel Corp 焼付硬化性に優れた良加工性高強度熱延鋼板とその製造方法
JP3039862B1 (ja) * 1998-11-10 2000-05-08 川崎製鉄株式会社 超微細粒を有する加工用熱延鋼板
CN1147609C (zh) 2000-04-07 2004-04-28 川崎制铁株式会社 具有优良应变时效硬化特性的钢板及其制造方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2618958C2 (ru) * 2012-03-23 2017-05-11 Зальцгиттер Флахшталь Гмбх Улучшаемая сталь без окалины, способ изготовления детали без окалины из этой стали и способ получения горячекатаной полосы из стали

Also Published As

Publication number Publication date
EP1394276A1 (fr) 2004-03-03
WO2002101099A1 (fr) 2002-12-19
CN1237189C (zh) 2006-01-18
JP4062961B2 (ja) 2008-03-19
DE60238118D1 (de) 2010-12-09
KR100859303B1 (ko) 2008-09-19
US20040231393A1 (en) 2004-11-25
JP2003055740A (ja) 2003-02-26
EP1394276A4 (fr) 2006-01-18
CN1514883A (zh) 2004-07-21
KR20030015890A (ko) 2003-02-25
US7485194B2 (en) 2009-02-03

Similar Documents

Publication Publication Date Title
EP3128027B1 (fr) Tôle en acier laminée à froid à grande résistance mécanique, ayant un rapport élevé de limite d&#39;élasticité, et son procédé de production
EP3214199B1 (fr) Tôle d&#39;acier hautement résistante, tôle d&#39;acier galvanisée à chaud hautement résistante, tôle d&#39;acier aluminiée à chaud hautement résistante ainsi que tôle d&#39;acier électrozinguée hautement résistante, et procédés de fabrication de celles-ci
EP2415893B1 (fr) Feuille d&#39;acier excellente en termes de maniabilité et son procédé de production
EP2589678B1 (fr) Tôle d&#39;acier à résistance élevée présentant une excellente aptitude au traitement ainsi que procédé de fabrication associé
EP2258886B1 (fr) Tôle d&#39;acier galvanisée par immersion à chaud, à haute résistance, présentant une excellente aptitude au traitement et son procédé de fabrication
EP2811047B1 (fr) Tôle en acier galvanisée par immersion à chaud, et procédé de fabrication de celle-ci
EP3508605B1 (fr) Tôle d&#39;acier haute résistance laminée à froid ayant d&#39;excellentes performances de phosphatation et son procédé de fabrication
EP2246456B1 (fr) Tôle d&#39;acier haute résistance et son procédé de production
EP3214193A1 (fr) Tôle d&#39;acier hautement résistante, tôle d&#39;acier galvanisée à chaud hautement résistante, tôle d&#39;acier aluminiée à chaud hautement résistante ainsi que tôle d&#39;acier électrozinguée hautement résistante, et procédés de fabrication de celles-ci
WO2022209519A1 (fr) Feuille d&#39;acier, élément, procédé de production d&#39;une feuille d&#39;acier et procédé de production d&#39;un élément
EP3239339A1 (fr) Acier traité thermiquement, produit moulé ultra-résistant ayant une excellente durabilité et procédé de fabrication correspondant
EP2604715A1 (fr) Tôle d&#39;acier laminée à froid, à haute résistance, dotée d&#39;une ouvrabilité et d&#39;une résistance aux chocs remarquables, et son procédé de fabrication
WO2001092593A1 (fr) Tole d&#39;acier laminee a froid presentant d&#39;excellentes proprietes de rheodurcissement par vieillissement, et procede de production
EP2426230A1 (fr) Tôle d&#39;acier zinguée à chaud à haute résistance présentant une excellente aptitude au façonnage, une excellente aptitude au soudage et d&#39;excellentes propriétés de résistance à la fatigue, et procédé de fabrication de cette dernière
US20170204490A1 (en) High-strength steel sheet and production method for same, and production method for high-strength galvanized steel sheet
EP3447159B1 (fr) Plaque d&#39;acier, plaque d&#39;acier plaquée et procédé pour les produire
EP2551366B1 (fr) Tube d&#39;acier à haute résistance soudé par résistance électrique et son procédé de fabrication
JP2023099015A (ja) 自動車用高強度冷間圧延鋼板
EP2792762A1 (fr) Tôle d&#39;acier laminée à froid haute résistance et à rapport d&#39;élasticité élevé et procédé permettant de produire cette dernière
WO2022172540A1 (fr) Tôle d&#39;acier hautement résistante, et procédé de fabrication de celle-ci
WO2021187321A1 (fr) Tôle d&#39;acier haute résistance et procédé de fabrication de celle-ci
EP3561121B1 (fr) Tôle d&#39;acier laminée à froid ayant une excellente aptitude au pliage et une excellente aptitude d&#39;expansion des trous et sont procédé de fabrication
WO2020162562A1 (fr) Tôle d&#39;acier revêtue de zinc par immersion à chaud et son procédé de fabrication
EP1394276B1 (fr) Feuille d&#39;acier laminee a chaud a haute resistance, presentant une resistance a l&#39;usure sur moule et des caracteristiques de fatigue excellentes
CN108713065B (zh) 高强度冷轧钢板及其制造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20031119

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LI LU MC NL PT SE TR

RTI1 Title (correction)

Free format text: HIGH TENSILE HOT-ROLLED STEEL SHEET EXCELLENT IN RESISTANCE TO SCUFF ON MOLD ANDIN FATIGUE CHARACTERISTICS

A4 Supplementary search report drawn up and despatched

Effective date: 20051206

17Q First examination report despatched

Effective date: 20080616

RTI1 Title (correction)

Free format text: HIGH TENSILE HOT-ROLLED STEEL SHEET EXCELLENT IN RESISTANCE TO SCUFF ON MOLD AND IN FATIGUE CHARACTERISTICS

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE FR

REF Corresponds to:

Ref document number: 60238118

Country of ref document: DE

Date of ref document: 20101209

Kind code of ref document: P

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20110728

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 60238118

Country of ref document: DE

Effective date: 20110728

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20120131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20110531

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20170516

Year of fee payment: 16

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 60238118

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20181201